Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D7/00—Modifying the physical properties of iron or steel by deformation
  • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
  • F28—HEAT EXCHANGE IN GENERAL
  • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
  • F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
  • F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
  • F28F21/081—Heat exchange elements made from metals or metal alloys
  • F28F21/082—Heat exchange elements made from metals or metal alloys from steel or ferrous alloys
  • F28F21/083—Heat exchange elements made from metals or metal alloys from steel or ferrous alloys from stainless steel
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/001—Austenite
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/004—Dispersions; Precipitations

Definitions

• This invention relates to an austenitic stainless steel which is excellent in high temperature strength.
• This stainless steel is useful for tubes of chemical plants, boilers of power plants and, for heat-resistant and pressure-resistant members, such as plates, bars, forged parts and the like.
• austenitic stainless steels such as SUS 304H, SUS 316H, SUS 321H, SUS 347H and SUS310S, which are standardized in JIS, have been conventionally used.
• SUS 304H, SUS 316H, SUS 321H, SUS 347H and SUS310S which are standardized in JIS.
• JIS Japanese Industrial Standard
• the use conditions of these devices under such a high temperature environment, have become remarkably severe. Accordingly, the required properties for this material have attained a higher level, and the conventional austenitic stainless steels are markedly insufficient in high temperature strength.
• Carbides are useful for improving high temperature strength, particularly creep strength of the austenitic stainless steel, and the strength enhancing effect of carbides, such as M 23 C 6 , TiC and NbC is practically used. Further improvement of creep strength by the addition of Cu is also applied because the fine Cu-phase, which precipitates during creeping, can contribute to the enhancing of creep strength.
• Patent Document 1 JP Kokai Sho 62-243742
• Patent Document 2 An austenitic stainless steel containing P of more than 0.06%, but not more than 0.20%, is disclosed in Patent Document 2.
• the steel has been developed for improving the resistance to salt damage under a high temperature environment. Accordingly, it contains an excessive amount of Si, more than 2.0% but not more than 4.0%. Such a large amount of Si promotes precipitation of the ⁇ -phase, and deteriorates the toughness and ductility of the steel.
• Patent Document 2 JP Kokai Hei 7-118810
• EP1342807 discloses an austenitic stainless steel tube with a uniform fine grained structure of regular grains, which is not changed to a coarse structure and the steam oxidation resistance is maintained even if the tube is subjected to a high temperature reheating during welding and high temperature bending working.
• the austenitic stainless steel tube consists of, by mass %, C: 0.03-0.12%, Si: 0.1-0.9%, Mn: 0.1-2%, Cr: 15-22%, Ni: 8-15%, Ti: 0.002-0.05%, Nb: 0.3-1.5%, sol.
• the austenitic stainless steel tube having austenitic grain size number of 7 or more and a mixed grain ratio of preferably 10% or less.
• EP1342807 (A2 ) also provide a method of manufacturing the austenitic stainless steel tube comprising the following steps: (a) heating an austenitic steel tube at 1100-1350 °C and maintaining the temperature, and cooling at a cooling ratio of 0.25 °C/sec; (b) working by cross-sectional reduction ratio of 10% or more at a temperature range of 500 °C or less; and (c) heating at a temperature range of 1050-1300 °C and at a temperature of lower by 10 °C or more than the heating temperature in the step(a).
• US4141762 (A ) mentions two-phase stainless steel containing 10 - 75% ferrite and an effective sulfur content controlled to 0.003% by weight or lower and an effective phosphorous content controlled to 0.01% by weight or lower.
• the first objective is to provide an austenitic stainless steel which is excellent in not only creep strength but also in creep ductility and weldability.
• the second objective is to provide an austenitic stainless steel which is excellent in hot workability in addition to the above-mentioned properties.
• the inventors have tried to improve creep ductility, weldability and hot workability by adding a small amount of elements to the steel containing P in order to increase high temperature strength.
• the inventors investigated elements that improve creep ductility of the austenitic stainless steel containing large amounts of P. As a result, it was found that the addition of very small amounts of REM, particularly Nd, can improve creep ductility remarkably, and also improve weldability and hot workability.
• the present invention is based on the above-mentioned founding, and it relates to austenitic stainless steels defined in the following (1) to (4).
• REM is abbreviation for rare earth elements and indicates 17 elements containing fifteen lanthanoid elements and Sc and Y.
• the stainless steels of the present invention can be broadly applied as tubes, plates, bars, castings, forged parts and the like, which need high temperature strength and corrosion resistance.
• C is an useful and important element because it is necessary for obtaining tensile strength and creep strength under a high temperature environment.
• the C content is below 0.05 %, the positive effect cannot be obtained and high temperature strength cannot reach the necessary level of the steel of this invention.
• it exceeds 0.15 % unsoluble carbides increase and C can no longer contribute to the improvement of high temperature strength, and additionally mechanical properties, such as toughness and weldability deteriorate. Accordingly, C content should be 0.05 to 0.15 %.
• a preferable upper limit is 0.13 %, and a more preferable upper limit is 0.12%.
• Si is an element that is added for the purpose of deoxidizing molten steel, and it is useful for improving oxidation resistance and steam oxidation resistance. It is preferable that the Si content is 0.05 % or more for attaining these effects. However, if the Si content is over 2 %, the precipitation of the intermetallic compounds, such as the ⁇ -phase is promoted and therefore the toughness and ductility deteriorate due to the degraded stability of structure at an elevated temperature. Further, weldability and hot workability also deteriorate. Therefore, the Si content should be not more than 2 %, and more preferably not more than 1 %.
• Mn likewise to Si, has a deoxidizing effect on the steel, and improves the hot workability by fixing S, which is an inevitable impurity of the steel. That is to say that Mn fixes S to form sulfide.
• an Mn content of not less than 0.1 % is essential. However, if the Mn content is over 3 %, the precipitation of intermetallic compounds, such as the ⁇ -phase, is promoted and the stability of structure, high temperature strength and other mechanical properties deteriorate. Therefore, the content of Mn should be 0.1 -3 %.
• a preferable lower limit and upper limit are 0.2 % and 2 % respectively. A more preferable upper limit is 1.5 %.
• P enhances creep strength of the steel of this invention, since P refines carbide and forms precipitates of compounds with Ti and Fe.
• the content of P should be not less than 0.05 % in order to obtain these effects.
• P generally deteriorates creep ductility, weldability and hot workability, this disadvantage decreases in the steel of this invention due to the addition of REM.
• the effects of REM, particularly Nd decrease when excessive P is contained in the steel. Therefore, the P content should be 0.3 % or less.
• the P content should be 0.05 to 0.3 %.
• a preferable lower limit and upper limit are 0.06 % and 0.25 % respectively, and a more preferable lower limit is more than 0.08 %.
• a more preferable upper limit is 0.20 %.
• S is an impurity that remarkably decreases the hot workability, S should be not more than 0.03 %, and the less, the better.
• Cr is an important element, which ensures oxidation resistance, steam oxidation resistance, high temperature corrosion resistance and the like. Furthermore, Cr forms Cr-carbide and increases the strength of the steel. Therefore, Cr should be not less than 15 %. The more the Cr content, the more corrosion resistance improves. However, the austenite phase becomes unstable and intermetallic compounds such as the ⁇ -phase and ⁇ -Cr phase, which deteriorate toughness and high temperature strength, may form easily when the Cr content exceeds 28 %. Therefore, Cr content should be 15 to 28 %. A preferable lower limit and upper limit are 16 % and 25 % respectively, and a more preferable lower limit and upper limit are 17 % and 23 % respectively.
• Ni is an indispensable element in order to ensure the stable austenite structure.
• the suitable lower limit of the Ni content is determined by the contents of the ferrite forming elements such as Cr, Mo, W and Nb and the austenite forming elements such as C and N.
• the Ni content should be 8 to 55 %.
• a preferable upper limit is 25 %, and a more preferable upper limit is 15 %.
• Cu is one of the elements enhancing the creep strength because it precipitates coherently with the austenite matrix as a fine Cu-phase during the use of the steel under a high temperature.
• the Cu may be contained.
• the Cu content should be 0 to 3.0 %.
• a preferable upper limit is 2.0 %, and a more preferable upper limit is 0.9 %.
• the lower limit of its content is preferably 0.01 % when the effect for improving creep strength is desired.
• Ti forms carbide and contributes to the improvement of high temperature strength.
• Ti together with P, forms a phosphide that contributes to creep strength.
• the Ti content should be 0.05 to 0.6 %.
• a more preferable lower limit and upper limit are 0.06 % and 0.5 % respectively.
• the content of Al depends upon the content of sol.Al, namely acid-soluble Al. Al is added for deoxidizing of the steel.
• the content of sol.Al should be not less than 0.001 % in order to ensure this effect.
• the sol.Al content should be 0.001 to 0.1 %.
• a preferable lower limit and upper limit are 0.005 % and 0.05 % respectively.
• a more preferable lower limit and upper limit are 0.01 % and 0.03 % respectively.
• TiN precipitates at a high temperature when N content exceeds 0.03 %.
• the TiN exists in the steel as coarse insoluble nitrides, and it deteriorates the hot workability and cold workability. Accordingly the N content should be 0.03 % or less, and the less, the better.
• a preferable upper limit is 0.02 %, and a more preferable upper limit is 0.015 %.
• Elements of REM are important for the steel of this invention.
• the addition of REM can restore the creep ductility and weldability, which are deteriorated by the addition of a large amount of P.
• REM should be added at a level of not less than 0.001% in order to produce the above effect.
• inclusions such as oxides increase when the REM content exceeds 0.5 %.
• the appropriate range of the REM content is 0.001 to 0.5 %.
• a preferable lower limit and upper limit are 0.005 % and 0.2 % respectively.
• a more preferable upper limit is less than 0.1 %.
• the element of the REM can be used alone, a mixture of rare earth elements, such as "mish metal", can also be used.
• a particularly preferable one is Nd.
• One of the steels of this invention is an austenitic stainless steel consisting of the above-mentioned elements and impurities.
• Another one of the steels of this invention is an austenitic stainless steel containing at least one element, for further increasing the high temperature strength, selected from Mo, W, B, Nb, V, Co, Zr, Hf and Ta. The following are description of these elements.
• Mo 0.05-5 %
• W 0.05-10 %
• Mo+(W/2) is not more than 5 %.
• Mo and W are not essential for the steel of this invention. However, these elements may be added if necessary, since they are effective in improving the high temperature strength and creep strength.
• the lower limit of the content should be 0.05 %. If they are added together, the lower limit should be not less than 0.05 % in total.
• Mo content and W content exceed 5 %and 10 % respectively, the effects are saturated and intermetallic compounds such as the ⁇ -phase are formed and the austenite phase becomes unstable. Accordingly, the hot workability deteriorates. Therefore, when either one or both of Mo and W are used, the upper limits should be 5 % for Mo, 10 % for W, and 5 % for "Mo+(W/2)".
• the content of W should preferably be less than 4 % in order to stabilize the austenite phase, since W is a ferrite forming element.
• B is contained in carbonitrides and also exists as free B along the grain boundaries, and contributes to the fine precipitation of carbonitride. B improves the high temperature strength and creep strength due to the suppressing of the grain boundary slip through the strengthening of grain boundaries.
• the content of not less than 0.0005 % is necessary for these effects. However, the weldability of the steel deteriorates if it is more than 0.05 %. Therefore, the B content should be 0.0005 to 0.05 %, if it is added.
• a preferable lower limit and upper limit are 0.001 % and 0.01 % respectively, and a more preferable upper limit is 0.005 %.
• Nb forms carbonitride and increases the creep strength.
• its content is less than 0.05 %, sufficient effects cannot be obtained.
• the Nb content should be 0.05 to 0.8%.
• a preferable upper limit is 0.6 %.
• V forms carbide and is effective in order to increase the high temperature strength and creep strength.
• the content is less than 0.02 %, the effect cannot be obtained.
• the content exceeds 1.5 %, the high temperature corrosion resistance decreases, and ductility and toughness deteriorate due to precipitation of a brittle phase. Therefore, the V content should be 0.02 to 1.5 %.
• a more preferable lower limit and upper limit are 0.04 % and 1 % respectively.
• Co stabilizes the austenite structure, likewise Ni, and also improves creep strength.
• the content is less than 0.05 %, the effect cannot be obtained.
• the content exceeds 5 %, the effect saturates and production cost increases. Accordingly, the Co content should be 0.05 % to 5 %, if it is used.
• Zr contributes to grain boundary strengthening and enhancing high temperature strength and creep strength. Furthermore, it fixes S to improve hot workability. Zr content of 0.0005 % or more is necessary for obtaining the effects. However, mechanical properties, such as ductility and toughness, deteriorate when its content exceeds 0.2 %. Accordingly, the Zr content should be 0.0005 to 0.2 %, when it is added.
• a preferable lower limit and upper limit are 0.01 % and 0.1 % respectively. A more preferable upper limit is 0.05 %.
• Hf is an element that contributes mainly to grain boundary strengthening and also increases creep strength. When its content is less than 0.0005 %, the effects cannot be obtained. On the other hand, when its content exceeds 1 %, workability and weldability are impaired. Thus the Hf content should be 0.0005 to 1 %, when it is added.
• a preferable lower limit and upper limit are 0.01 % and 0.8 % respectively, and a more preferable lower limit and upper limit are 0.02 % and 0.5 % respectively.
• Ta forms carbonitride and enhances high temperature strength and creep strength as a solid-solution strengthening element.
• the Ta content should be 0.01 to 8 %, when it is added.
• a preferable lower limit and upper limit are 0.1 % and 7 % respectively, and a more preferable lower limit and upper limit are 0.5 % and 6 % respectively.
• Another one of the steels of this invention is an austenitic stainless steel that contains at least one of Ca and Mg in addition to the above-mentioned elements.
• Ca and Mg improve hot workability of the steel of this invention as mentioned below.
• Mg and Ca form sulfide by fixing S, which impairs the hot workability of the steel, they improve the hot workability. When contents of each are less than 0.0005 %, the effects cannot be obtained. On the other hand, Mg and Ca of more than 0.05 % respectively deteriorate the steel quality and impair the hot workability and ductility. Accordingly, in the case where Mg and/or Ca are added, the content of each should be 0.0005 to 0.05 %.
• a preferable lower limit and upper limit are 0.001 % and 0.02 % respectively, and a more preferable upper limit is 0.01 %.
• Ingots are prepared in the conventional melting and casting process for stainless steel.
• the ingots, as cast or after forging and blooming into billets, are hot-worked in the process such as a hot extrusion or a hot rolling.
• the heating temperature before the hot working is 1160 to 1250°C
• the finishing temperature of the hot working is preferably not lower than 1150°C. It is also preferable to cool the hot worked products at a large cooling rate of 0.25°C/sec or more, in order to suppress the precipitation of coarse carbonitrides.
• a final heat treatment may be carried out, however, cold working may be added, if necessary.
• Carboniterides should be dissolved by heat treatment before the cold working. It is desirable to carry out the heat treatment at a temperature which is higher than the lowest temperature of the heating temperature before the hot working and the hot working finishing temperature.
• the cold working is preferably performed by applying a strain of 10% or more, and two of more cold workings may be carried out.
• the heat treatment for finished products is carried out at a temperature in a range of 1170 to 1300°C.
• the temperature is preferably higher than the finishing temperature of the hot working or the above-mentioned heat treat temperature by 10°C or more. It is preferable that the products are cooled, after the final heat treatment, at a cooling rate of 0.25°C/sec or more in order to suppress the precipitation of coarse carbonitrides.
• Steels having the respective chemical compositions shown in Table 1 were melted by use of a high-frequency vacuum furnace, and cast to produce ingots of 30 kg weight and 120 mm diameter.
• Steels Nos.1 to 19 in Table 1 are the steels according to the present invention, and steels A to F are comparative examples.
• Each steel ingot was hot-forged to give a plate of 40 mm thickness.
• a bar test piece of 10 mm diameter and 130 mm length was prepared by machining the plate.
• the plate was further hot-forged into a plate of 15mm thickness. After softening heat treatment, the plate was cold-rolled into 10mm thickness and heated at 1150°C for 15 minutes and water-cooled.
• the creep test piece was a round bar of 6 mm diameter and 30 mm gauge length
• the Varestraint test piece was a plate of 4 mm thickness, 100 mm width and 100 mm length.
• the contents of P were varied in the steels A, B and C of comparative examples.
• the content of P is restricted to 0.040 % or less for the stainless steel for boiler tubes as shown in JIS G3463 for example. Accordingly, the P content of steel A is at the conventional P content level.
• Table 2 the creep strength increases with the increase of the P content, however the area of reduction after rupture, weldability and high temperature ductility remarkably decrease.
• Steels Nos.1 to 4 and No.19 are the steels of this invention. Creep rupture strength of these steels is improved by addition of P, likewise the comparative steels B and C. In these steels, differing from comparative steels, there is no decrease of creep ductility, weldability and high temperature ductility because of the addition of Nd, La and Ce. Further, the creep ductility of these steels is superior to that of steel A, in which the P content remains at the conventional level.
• Steel D is a steel used for a comparative example without the Ti addition and contains P and Nd in amounts approximately equal to that of steel No.2 of this invention. However, its creep properties are not sufficient because it does not contain Ti. Steels Nos.5 and 6 are further improved in creep strength by the addition of Cu. Comparative steel E contains Cu of more than 3.0 %. It is apparent that the excessive amount of Cu impairs the effects of Nd, i.e., effects for improving creep ductility, weldability and high temperature ductility. On the basis of this fact, it can be understood that the Cu content should be not more than 3.0 %.
• the steel of this invention may further contain one or more of W, Mo, B, Nb, V, Co, Zr, Hf, Ta, Mg and Ca.
• High temperature ductility and creep rupture strength can be further improved by the addition of these elements as shown by steels Nos.7 to 18.
• the austenitic stainless steel is remarkably improved not only in high temperature strength but also in hot workability because it contains P and REM, particularly Nd. Further, the steel is excellent in toughness under long period use at high temperatures.
• the steel is useful for heat resistant and pressure resistant members which are used under a high temperature of 650 to 700°C or higher. In a plant using this steel, the cost of production can be markedly reduced, since the production efficiency can be maintained at a higher level.

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• 2006
  • 2006-03-31 KR KR1020077022019A patent/KR100931448B1/ko active IP Right Grant
  • 2006-03-31 DK DK06730842.9T patent/DK1867743T5/da active
  • 2006-03-31 CN CN200680010751.5A patent/CN100577844C/zh not_active Expired - Fee Related
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